3C-SiC is considered an attractive material for power electronics devices due to its excellent properties such as higher theoretical electron mobility (~900 cm 2 V -1 s -1 ) and lower interface state density between SiC and SiO 2 when compared to the most technological mature 4H-SiC polytype. Both these properties make 3C-SiC very attractive for metal-oxide -semiconductor field effect transistors (MOSFETs) working in medium-and high-power regimes [1]. Moreover, single crystal 3C-SiC is grown at a lower temperature than 4H-SiC and heteroepitaxy with large-area Si substrates is allowed, thus reducing drastically the cost for its production [2]. The epitaxy of doped 3C-SiC films is easily achievable by using gaseous dopants during the growth process with nitrogen and aluminium as most used doping species [3,4]. A much harder step is the definition of localized doping region underneath the drain and/or source for MOSFET realization. The most used technique to obtain such structures is to implant N, Al or B ions in the desired regions [5,6]. For p-type doping, Al is preferred due to its shallow energetic levels and, consequently, lower activation energy (0.24 eV). Ion implantation processing, on the other hand, involves the scattering of the ordered atoms in SiC lattice with high-energetic ions (from tenth to thousands keV) resulting in a damaging of the crystal structure of the hosting material.In this study, a 10 μm thick 3C-SiC film has been processed to realize an Al + -implanted layer underneath the film surface. The structural damaging and recovery due to the implantation processing and subsequent thermal annealing have been evaluated by means of X-ray diffraction (XRD) and micro-Raman spectroscopy (μ-Raman). Reciprocal space mapping (RSM) of the (004) 3C-SiC reciprocal lattice point (RLP) was then used to further study the recovery at different temperatures.3C-SiC was grown in a chemical vapor deposition (CVD) reactor by using a multi-step growth process [7]. 3C-SiC growth process was performed on a (001)-oriented Si substrate by using ethylene (C 2 H 4 ), trichlorosilane Damaging in Al-implanted 3C-SiC and subsequent crystal recovery due to thermal treatments up to 1350 °C are evaluated by X-ray diffraction and micro-Raman spectroscopy. Reciprocal space mapping of (004) 3C-SiC planes shows a lowintensity implantation-induced secondary peak at higher interplanar spacing in the as-implanted 3C-SiC sample, with a generated misfit between the implanted and the epitaxial region of about 0.6%. Increasing the annealing temperature from 950 °C to 1350 °C, the secondary peak is gradually reabsorbed within the epitaxial 3C-SiC reciprocal lattice point. Finally, the disappearance of the secondary peak after a 1350 °C thermal treatment is observed. Thus, implantationinduced average strain, resulting in a severe 3C-SiC deforma-tion, has been totally relieved at the highest annealing temperature.